Imaging apparatus and image forming apparatus having continuous pores in three dimensions in porous body

ABSTRACT

An imaging apparatus for imaging a subject image from a lens on an imaging element through an optical filter has a porous body having pores which three dimensionally communicate with each other at least at a side opposite to the imaging element of the optical filter.

CROSS-REFERENCE TO RELATED APPLICATION

This application is a Continuation of U.S. application Ser. No.13/532,288, filed Jun. 25, 2012, which claims priority from JapanesePatent Application No. 2011-146512 filed Jun. 30, 2011 and No.2012-126379 filed Jun. 1, 2012, which are hereby incorporated byreference herein in their entirety.

BACKGROUND OF THE INVENTION

1. Field of the Invention

One disclosed aspect of the embodiments relates to an imaging apparatusand an image forming apparatus employing a porous body for suppressingadhesion of foreign substances, such as dust.

2. Description of the Related Art

In imaging apparatuses, such as a digital camera etc, a photographingluminous flux is received by an imaging element, such as a CCD or aC-MOS, and then a photoelectric conversion signal output from theimaging element is converted to image data to be recorded in a recordingmedium, such as a memory card.

In such an imaging apparatus, a low pass filter or an infrared ray cutfilter is disposed at the side of a subject of the imaging element.Particularly in a digital single-lens reflex camera in which the lensmay be exchanged, a mechanical operation portion, such as a shutter, isdisposed near an optical filter, such as a low pass filter, and foreignsubstances, such as dust generated from the operation portions,sometimes adhere to the low pass filter or the like. Moreover, dust orthe like enters the camera main body from an aperture of a lens mount,and sometimes adhere to the low pass filter or the like duringexchanging the lens. When dust adheres to the optical filter, such as alow pass filter, the adhesion point appears in a captured image as ablack (gray) point, which sometimes reduces the quality of the capturedimage.

As a former technique for solving the problems, Japanese PatentLaid-Open No. 2002-204379 discloses a technique in which a dustprooffilm is provided at the side of a subject of an imaging element, and thedustproof film is vibrated by a piezoelectric element to remove dust.Moreover, Japanese Patent Laid-Open No. 2006-163275 discloses atechnique in which the surface is coated in such a manner that dust orthe like is hard to adhere.

In image forming apparatuses, such as an electrophotographic copyingmachine and an electrophotographic printer, a photoconductor isirradiated with laser light to form an electrostatic latent image. Then,the electrostatic latent image is developed with a toner, the tonerimage to be obtained is transferred onto a sheet-like recording medium,and thereafter the toner is heated and fixed with a fixing apparatus tothereby form an image on the recording medium.

Such an image forming apparatus has, in a housing, a light source whichemits laser light based on image information, a rotary polygon mirrorfor deflecting and scanning the laser light emitted from the lightsource, an Fθ lens by which the laser light deflected and scanned by therotary polygon mirror is imaged on a photoreceptor, a reflecting mirror,and the like. The image forming apparatus further has an opticalapparatus which irradiates a photoconductor with laser light from anaperture in the housing. When there is dirt on a laser optical path,image omission arises at a portion corresponding to the dirt on theimage, which sometimes reduces the image quality. Therefore, anapparatus has been proposed in which the entrance of dust, a toner, orthe like is prevented by sealing the housing, and a transparentdustproof glass is attached to the aperture of the housing which emitslaser light and a shutter is provided thereto, whereby dirt of thedustproof glass is prevented (Japanese Patent Laid-Open No. 11-167080).

Japanese Patent Laid-Open No. 2002-204379 mentioned above discloses amethod for vibrating a dustproof film to thereby remove foreignsubstances, in which, in order to remove the foreign substance adheringto the dustproof film, high energy is required and also the structurebecomes complicated.

The method in which the surface is coated in such a manner that dust orthe like becomes difficult to adhere to the surface described inJapanese Patent Laid-Open No. 2006-163275 requires the formation of aplurality of optical films as an antireflection film for maintaining theoptical performance.

According to the method in which the shutter is provided described inJapanese Patent Laid-Open No. 11-167080, the apparatus is easily damagedand also the structure becomes complicated.

Moreover, dust removal may not be satisfactorily achieved by the formertechniques, and a further dust reduction has been required.

SUMMARY OF THE INVENTION

One disclosed aspect of the embodiments provides an imaging apparatusand an image forming apparatus employing a porous body having highstrength, low reflection, and excellent dust proof property.

In order to solve the above-described problems, the imaging apparatus isan imaging apparatus for imaging a subject image from a lens on animaging element through an optical filter and has a porous body havingpores which three dimensionally communicate with each other at least ata side opposite to the imaging element of the optical filter.

The image forming apparatus is an image forming apparatus having anoptical apparatus for forming an image by emitting light, in which aleast one portion of a dustproof glass provided in the optical apparatusis a porous body having pores which three dimensionally communicate witheach other.

One embodiment may provide an imaging apparatus and an image formingapparatus employing a porous body having high strength, low reflection,and excellent dust proof property.

Further features of the disclosure will become apparent from thefollowing description of exemplary embodiments with reference to theattached drawings.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a view explaining an imaging apparatus according to oneembodiment.

FIG. 2 includes electron microscope observation views explaining aporous body according to one embodiment.

FIG. 3 is a graph showing a dustproof effect.

FIGS. 4A and 4B are views explaining liquid crosslinking.

FIGS. 5A and 5B are views explaining the pore diameter and the skeletondiameter.

FIG. 6 is a view explaining an optical member according to oneembodiment.

FIGS. 7A and 7B illustrate an example of a foreign substance removalapparatus provided in the imaging apparatus according to one embodiment.

FIG. 8 is a view illustrating an example of a piezoelectric element.

FIG. 9 is a view illustrating an example of the vibration principle ofthe piezoelectric element according to one embodiment.

FIGS. 10A and 10B are schematic views illustrating the vibrationprinciple of the foreign substance removal apparatus provided in theimaging apparatus according to one embodiment.

FIG. 11 is a view explaining an image forming apparatus according to oneembodiment.

FIG. 12 is a view explaining the porosity.

DESCRIPTION OF THE EMBODIMENTS

Hereinafter, suitable embodiments are described in detail with referenceto the attached drawings. However, the embodiments do not limit thescope of the disclosure.

First Embodiment

As a first embodiment, an imaging apparatus employing a porous body,specifically an imaging apparatus for imaging a subject image from alens on an imaging element through an optical filter, is described. FIG.1 is a view illustrating one embodiment of the imaging apparatus. FIG. 1includes an imaging apparatus 6 and a lens 31 which is detachablyattached to the imaging apparatus 6. In imaging apparatuses, such as adigital single lens reflex camera, photographing image screens ofvarious field angles may be obtained by changing photographic lenses foruse in photographing to lenses different in the focal lengths. Thereference numeral 4 denotes an imaging element. The reference numeral 5is a porous body, the reference numeral 32 denotes a low pass filter,and the reference numeral 33 denotes an infrared ray cut filter. Theimaging element 4 is housed in a package (not illustrated), and thepackage holds the imaging element in the sealing state with a coverglass (not illustrated). In the optical path ranging from an imagingoptical system in the removal lens 31 to the imaging element 6, the lowpass filter 32 is provided which limits the cut-off frequency of theimaging optical system in such a manner that spatial frequencycomponents which are higher than necessary of an object image are nottransmitted onto the imaging element 4. Moreover, the infrared cutfilter 33 is also formed. The space between the optical filter, such asthe low pass filter or the infrared cut filter, and the cover glass (notillustrated) forms a sealed structure (not illustrated) with a sealingmember, such as a double-stick tape. Thus, it is configured such thatdust generated outside the imaging apparatus or in the imaging apparatusdoes not enter the space between these optical filters and the coverglass. This embodiment describes an example having both the low passfilter and the infrared cut filter as the optical filter but either oneof the low pass filter or the infrared cut filter may be provided. Theporous body may be integrally formed as a film on a base material. Thebase material may be a crystal in the low pass filter 32 or may be aheat-resistant glass, such as quartz glass, 7059 glass of Corning, Inc.,or Neoceram N-0 of Nippon Electric Glass Co., Ltd. The heat-resistantglass refers to a base material which may bear a process for forming theporous body, and may be subjected to matching of the thermal expansionwith the porous body and the adjustment of the film thickness. Theporous body 5 is disposed at least at the side opposite to the imagingelement 4 of the optical filter. In other words, the porous body 5 isdisposed at a side near the removable lens 31 of the optical filter.More specifically, the porous body 5 is disposed at the environment ofthe vicinity of the attachment portion of the removable lens. In thevicinity of the environment, a mechanical operation portion, such as ashutter, is disposed, so that foreign substances, such as dust,generated from the operation portions, sometimes adhere to the low passfilter and the like. Moreover, when exchanging the lens, dust or thelike sometimes enters the camera main body from an aperture of a lensmount, and adhere thereto. Thus, dust, dirt, and the like easily enter,so that the apparatus is likely to contact foreign substances to beeasily damaged. It is a matter of course that the porous body may bedisposed at any place of the imaging apparatus where dust is easilyattached. Moreover, a foreign substance removal apparatus for applyingvibration or the like to the porous body to thereby remove the foreignsubstances may also be provided.

Next, the porous body is described. FIG. 2 includes electron microscopeobservation views of the porous body surface. In FIG. 2, the referencenumeral 1 denotes pores, in which continuous pores are formed whilebending in the horizontal direction of the sheet toward the inside ofglass (perpendicular direction of the sheet). The reference numeral 2denotes the skeleton forming the pores and contains silicon oxide, forexample. FIG. 2 includes electron microscope observation views of theporous body surface, in which the same pores and the skeleton are formedalso in the glass. In this description, the pores which communicate witheach other while bending in the horizontal direction of the sheet towardthe inside of the glass (perpendicular direction of the sheet) asillustrated in FIG. 2 are referred to as the pores which threedimensionally communicate with each other. The skeleton 2, i.e., thestructure in which the skeleton is continuous while three dimensionally(perpendicular direction and horizontal direction of the sheet)complicatedly bending as illustrated in FIG. 2 is referred to as aspinodal structure. The spinodal structure means a porous structurederived from spinodal type phase separation. The porous body forms thepores which three dimensionally communicate with each other by theskeleton which is continuous while three dimensionally complicatedlybending. In other words, the porous body has three dimensionallycontinuous network pores. The porous body having such a characteristicshape is obtained by, for example, removing one phase of a phaseseparated glass which is phase separated into two phases.

In the porous body having network pores which three dimensionallycommunicate with each other, since the skeleton (portion other than thepores) is densely present not only in the film thickness direction butin the direction perpendicular to the film thickness direction,sufficient strength is obtained. For example, although the case wherehuman beings (or machines) directly touch foreign substances adhering tothe porous body and remove the same may be considered, strength issufficiently high so that the surface structure is not destroyed evenwhen the foreign substances are removed using cleaning members, such asrubber or fiber.

FIG. 3 is a view obtained by measuring the number of foreign substancesadhering to the surface after applying 25 KPa air pressure and 50 KPaair pressure to silica glass having no pores in the surface and theporous body before measurement (initial stage), and graphing the numberof the foreign substances. It is found that foreign substances hardlyadheres to the porous body from the initial stage (before applying airpressure) as compared with the silica glass having no pores in thesurface. Some reasons why the porous body has an excellent dustproofeffect are considered. In the silica glass having no pores in thesurface, the power of sucking dust, dirt, and the like generates on theentire glass surface. However, in the porous body, the sucking powergenerates only on the skeleton portions of the porous body. Therefore,it is considered that the sucking power may be weakened. Moreover, thepores of the porous body are three dimensionally entangled toward theinside and communicate with each other, and thus is excellent inbreathability. It is considered that this also plays a role ofpreventing the adsorption of dust, dirt, and the like to the surface.Moreover, the porous body demonstrates an excellent dustproof effect dueto lowered liquid crosslinking as shown thereafter.

FIGS. 4A and 4B schematically illustrate the adsorbability obtained byliquid crosslinking. When a liquid 73 is present between an object 71and a dust 72, liquid crosslinking is formed between the object 71 andthe dust 72, so that the pressure of the inside of the air interface ofthe liquid crosslinking and the pressure of the outside thereof aredifferent from each other, and the pressure at the liquid side is low.When the pressure at the air side is equal to the atmospheric pressure,the pressure at the liquid side becomes a negative pressure in which thepressure is lower than the atmospheric pressure. It is known that thenegative pressure is represented by Equation (1). It is also known thatthe sucking power is represented by Equation (2), and is a valueobtained by multiplying the negative pressure p by the area S, which canbe related to total area S0 and contact fraction α.

In the equation, R1 is the radius of curvature of the air interface ofthe liquid 73 formed between the object 71 and the dust 72 and R2 is theradius of the contact region of the object 71 and the liquid 73.

$\begin{matrix}{{Negative}\mspace{14mu}{pressure}} & {{p = {\sigma\left( {\frac{1}{R\; 1} - \frac{1}{R\; 2}} \right)}}\mspace{236mu}} & (1) \\{{Sucking}\mspace{14mu}{power}} & {F - {pS} - {{pS}\; 0\left( {1 - \alpha} \right)}} & (2)\end{matrix}$

FIG. 4A illustrates the case where the surface of the object 71 issmooth, in which R2 is the radius R of dust. FIG. 4B illustrates thecase where an object 81 is a porous body, in which R2 is the half of theskeleton diameter R′ of the porous body.

In order to reduce the sucking power, the value of R2 may be broughtclose to the value of R1, i.e., the contact surface of the object 71 (or81) and the liquid 73 may be reduced. In FIG. 4B, R1 is determined basedon the irregularities of the contact portion and the capillarycondensation on the surface but is considered to be close to about 10nm. While, in the porous body, the value of R2 is not determined by thedust size 2R, but by the skeleton diameter 2R′ of the porous body. Sincethe skeleton diameter 2R′ is smaller than the dust size 2R, the suckingpower may be much more reduced. Moreover, the sucking power may befurther reduced also by increasing the porosity or a.

As described above, in order for the porous body to maintain thestrength and to obtain a dustproof effect, it is desirable that theaverage skeleton diameter of the porous body surface is 5 nm or more 80nm or lower. More suitably, it is desirable that the average skeletondiameter is 5 nm or more and 50 nm or lower. The average skeletondiameter is defined as the average value of the minor axis in aplurality of ellipses by which the skeleton of the porous body surfaceis approximated. Specifically, as illustrated in, for example, FIG. 5B,the value is obtained by approximating the skeleton 2 by a plurality ofellipses 13 with reference to the electronograph of the porous bodysurface, and then calculating the average value of the minor axis 14 ineach ellipse. At least 30 or more points are measured, and the averagevalue thereof is determined. The measurement is not performed for theentire porous body and may be performed in desired regions. When theaverage skeleton diameter is smaller than 5 nm, the formation becomesdifficult and when the average skeleton diameter is larger than 80 nm,the dustproof effect tends to decrease. When the average skeletondiameter is 50 nm or lower, a higher dustproof effect is demonstrated.

It is desirable that the average pore diameter of the porous bodysurface is 5 nm or more and 500 nm or lower, particularly 10 nm or moreand 100 nm or lower, and further 15 nm or more and 80 nm or lower. Theaverage pore diameter is defined as the average value of the minor axisin a plurality of ellipses by which the pores of the porous body surfaceare approximated. Specifically, as illustrated in, for example, FIG. 5A,the value is obtained by approximating the pores 1 by a plurality ofellipses 11 with reference to the electronograph of the porous bodysurface, and then calculating the average value of the minor axis 12 ineach ellipse. At least 30 or more points are measured, and the averagevalue thereof is determined.

Furthermore, when considering the mechanical properties, it is desirablethat the porosity of the porous body is usually 10% or more and 80% orlower and particularly 20% or more and 75% or lower. The porosity inthis description is defined as the proportion of the pores when the areaof the porous body surface is set to 1. Specifically, treatment forperforming binarization with the skeleton portions and the pore portionswith reference to the electronograph of the porous body surfacecontaining the porous body as illustrated in FIG. 1, and determining thesame from the ratio. When the porosity is 80% or lower, the mechanicalproperties may be demonstrated and a dustproof function is alsodemonstrated.

When an antireflection function is required, the reflection on theinterface with the air is reduced when the porosity is increased. Inthis case, the porosity is suitably 30% or more and more suitably 50% ormore. Since the porous body has skeleton which is continuous while threedimensionally complicatedly bending, the strength does not decrease evenwhen the porosity is increased. Therefore, the refractive index may belowered while maintaining the strength. Thus, the porous body may beprovided which has excellent antireflection performance and also hasstrength with which the surface is not damaged even when touching thesurface.

The shape of the porous body is not particularly limited and, forexample, a plate like porous body, a porous body having a curvedsurface, and an aspect in which a porous body is formed on a basematerial are mentioned. These shapes may be selected as appropriate.Usable for the base material are base materials having heat resistance,such as quartz glass, 7059 glass of Corning, Inc., Neoceram N-0 ofNippon Electric Glass Co., Ltd., sapphire, crystal, and the like. Anaspect may also be suitably used in which the porous body is directlyformed on a crystal used in a low pass filter. Since excellentantireflection performance is imparted, it is not necessary toseparately provide an antireflection film, and an optical member havingoptical performance with an excellent antireflection effect and anexcellent dustproof effect on the surface may be obtained.

Next, with respect to the aspect in which a porous body is integrallyformed on a base material, the outline structure thereof is described asfollows. This aspect is referred to as an optical member in thisdescription. In FIG. 6, an optical member 101 has a porous body 102having the pores which three dimensionally communicate with each otheras described in the first embodiment on a base material 103. However, anoptical member containing only the porous body 102 is not excluded.

Since the optical member 101 has the porous body 102 having the poreswhich three dimensionally communicate with each other on the surface,the optical member 101 has surface properties having both high surfacestrength and high porosity and also has high dustproof performance. Theoptical member 101 may achieve higher strength by the use of the basematerial 103. Furthermore, since the porous body is formed on the basematerial, the thickness of the porous body may be controlled. Asrequired, the porosity of the pores continuously or intermittently mayvary entirely or partially in the porous body.

In the optical member, the boundary of the porous body and the basematerial is clear. Therefore, when used as an optical member, a varianceof each sample decreases, so that high design accuracy may be realized.Although the details are described later, a porous body having poresaccording to the purpose may be formed by arbitrarily changing the heattreatment conditions during manufacturing (heat treatment conditions forcausing phase separation).

The optical member has the skeleton of the spinodal structure, in whichthe porous body surface and the base material are continuously connectedthrough the continuous pores. Therefore, various application anddevelopment may be achieved in which the features of the base materialand the spinodal structure are utilized by the use of arbitrary porediameters and arbitrary base materials.

The thickness of the porous body is not particularly limited and issuitably 0.05 μm or more and 200.00 μm or lower and more suitably 0.10μm or more and 50.00 μm or lower. When the thickness is smaller than0.05 μm, there is a tendency that the formation of the spinodalstructure becomes difficult and when the thickness is larger than 200.00μm, there is a possibility that the manufacturing cost for the formationof the porous body becomes high.

As the shape of the base material, base materials having any shape maybe used insofar as the porous body may be formed. As the shape of thebase material, a base material having a curvature may be acceptable.

The softening temperature of the base material is suitably equal to orhigher than the heating temperature for phase separation for forming thespinodal structure of the porous body described later and is moresuitably equal to or higher than a temperature obtained by adding 100°C. to the heating temperature for phase separation. However, when thebase material is a crystal, the melting temperature is the softeningtemperature. When the softening temperature is lower than thetemperature for forming the spinodal structure of the porous body, thebase material deforms during a heat treatment process for phaseseparation, and therefore the temperature is not suitable. The heatingtemperature for phase separation for forming the spinodal structurerepresents the maximum temperature among temperatures for forming theporous body (porous glass layer) of the spinodal structure.

It is suitable that the base material has resistance to etching of aglass layer.

In the optical member, the refractive index may be arbitrarily changedby controlling the porosity, and further the thickness of the porousbody (porous glass layer) may be arbitrarily changed.

The imaging apparatus may have a foreign substance removal apparatus asdescribed above. FIGS. 7A and 7B are schematic views illustrating anexample of a foreign substance removal apparatus 470. The foreignsubstance removal apparatus 470 is constituted by a vibration member410, a flexible printed circuit board 420 connected to a piezoelectricelement 430, and a fixation member referred to as sealing member 450,and is attached to a support 501 having an imaging element and the like.The piezoelectric element 430 and the vibration member 410 are fixed tothe plate surface of the vibration member 410 with a first electrodesurface of the piezoelectric element 430 as illustrated in FIG. 7B. Theflexible printed circuit board 420 is electrically connected to aportion of a second electrode surface 437 of the piezoelectric element430, so that an alternating voltage may be applied to the piezoelectricelement 430 from the power supply. Although the details are describedlater, the vibration member 410 is vibrated by the application of thealternating voltage. When the foreign substance removal apparatus 470 isprovided in contact with the porous body, foreign substances, such asdust and dirt, are hard to adhere to the porous body and further theforeign substances may be efficiently removed therefrom by applyingvibration or the like by the foreign substance removal apparatus.

FIG. 8 is a view illustrating an example of the piezoelectric element430 provided in the foreign substance removal apparatus. Thepiezoelectric element 430 is constituted by a piezoelectric material431, a first electrode 432, and a second electrode 433, in which thefirst electrode 432 and the second electrode 433 are disposed facingeach other to the plate surface of the piezoelectric material 431. Thesurface where a first electrode 432 is disposed at the front of thepiezoelectric element 430 of (c) at the right side in FIG. 8 is thefirst electrode surface 436 and the surface where the second electrode432 is disposed at the front of the piezoelectric element 430 of (a) atthe left side in FIG. 8 is the second electrode surface 437. Herein, theelectrode surface refers to the surface of the piezoelectric elementwhere the electrode is placed. For example, as illustrated in FIG. 8,the first electrode 432 may turn around the second electrode surface437. Furthermore, a third electrode and the like to be utilized forsensing or the like may be provided on the second electrode surface.

The first electrode 432 and the second electrode 433 contain aconductive layer having a thickness of about 5 nm to about 5000 nm. Thematerials thereof are not particularly limited, and materials usuallyused for the piezoelectric element may be acceptable. For example,metals, such as Ti, Pt, Ta, Ir, Sr, In, Sn, Au, Al, Fe, Cr, Ni, Pd, Ag,and Cu, and compounds thereof may be mentioned. The first electrode 432and the second electrode 433 may be one containing one of them or one inwhich two or more kinds thereof are laminated. The first electrode 432and the second electrode 433 may contain different materials.

FIG. 9 is a view illustrating an example of the operation principle ofthe piezoelectric element 430 provided in the foreign substance removalapparatus. In the piezoelectric element 430, the piezoelectric material431 is polarized beforehand in the perpendicular direction of the firstelectrode surface 436, so that a high frequency voltage may be appliedto the first electrode 432 and the second electrode 433 from the powersupply. The piezoelectric element 430 causes stretching vibration in thelength direction of the piezoelectric element 430 by elastic distortionof the piezoelectric material 431 caused by an alternating electricfield generated in the direction indicated by the arrow of an electricfield direction 435. The magnitude of the stretching vibration in thelength direction of the piezoelectric element is closely related to themagnitude of the piezoelectric displacement resulting from thepiezoelectric transversal effect of piezoelectric ceramics. Thereference numeral 434 represents the polarization direction.

FIGS. 10A and 10B are schematic views illustrating an example of thevibration principle of the foreign substance removal apparatus 470. Forconvenience, FIGS. 10A and 10B illustrate only the piezoelectric element430 and the vibration member 410. FIG. 10A illustrates a state wherealternating voltages having the same phase are applied to a pair ofright and left piezoelectric elements 430 to thereby cause out-of-planevibration of a standing wave in the vibration member 410. In the pair ofright and left piezoelectric elements 430, the polarization direction ofthe piezoelectric material 431 is the same as the thickness direction ofthe piezoelectric element 430, and the foreign substance removalapparatus 470 is driven at a seventh-order vibration mode. Herein, thevibration mode refers to a multiple order standing wave having aplurality of nodes or antinodes that may be generated by theout-of-plane vibration of the vibration member or a progressive wave inwhich nodes or antinodes move in the length direction of the vibrationmember 410 in a certain time.

FIG. 10B illustrates a state where opposite-phase alternating voltageswhose phases are 180° opposite to each other are applied to the one pairof right and left piezoelectric elements 430 through the flexibleprinted circuit board 420 to cause out-of-plane vibration of a standingwave in the vibration member 410. In the pair of right and leftpiezoelectric elements 430, the polarization direction of thepiezoelectric material 431 is the same as the thickness direction of thepiezoelectric element 430, and the foreign substance removal apparatus470 is driven at a sixth-order vibration mode. Thus, the foreignsubstance removal apparatus 470 of this embodiment may more efficientlyremove dust adhering to the surface of the vibration member 410 byeffectively using at least two vibration modes.

However, the foreign substance removal apparatus 470 usable is notalways driven at such vibration modes. For example, one piezoelectricelement 430 may be provided in the vibration member 410 and, in the onepair of right and left piezoelectric elements 430, the polarizationdirection of the piezoelectric material 431 does not need to be same asthe thickness direction of the piezoelectric elements 430. Furthermore,not the sixth or seventh vibration mode described above but anothervibration mode, such as an 18th or 19th vibration mode, may be utilizedand three or more kinds of vibration modes may be utilized. FIGS. 10Aand 10B illustrate the vibration principle using the vibration mode of astanding wave but a vibration mode using not a standing wave but aprogressive wave in which an arbitrary frequency and an arbitrary phaseare controlled may be used. It is suitable to select a peculiar mode inwhich the resonance frequency of the out-of-plane vibration to begenerated in the vibration member 410 is outside the audible region insuch a manner that the foreign substance removal apparatus 470 does notgenerate an unpleasant sound.

The foreign substance removal apparatus 470 may be disposed at any placeinsofar as the foreign substance removal apparatus 470 is placed betweenthe imaging element 4 and the porous body 5 of the imaging apparatusillustrated in FIG. 1. For example, the foreign substance removalapparatus 470 may be provided in such a manner that the vibration member410 contacts the porous body 5, that the vibration member 410 contactsthe low pass filter 32, or that the vibration member 410 contacts theinfrared cut filter 33. In particular, when provided contacting theporous body 5, foreign substances may be more efficiently removed asdescribed above. The vibration member 410 of the foreign substanceremoval apparatus 470 may be integrally formed with the porous body 5 oroptical filters, such as the low pass filter 32 or the infrared cutfilter 33. The vibration member 410 may also contain the porous body 5and may have functions of the low pass filter 32, the infrared cutfilter 33, and the like.

Second Embodiment

Next, an image forming apparatus employing the porous body described inthe first embodiment, specifically an image forming apparatus having anoptical apparatus used for emitting light to form an image, isdescribed.

FIG. 11 illustrates an example of the image forming apparatus. FIG. 11includes an optical apparatus 21 for irradiating a photoconductive drumwith laser light based on image information sent from an image scanner,a personal computer, or the like. The reference numeral 22 denotes adevelopment machine which forms a toner image on the photoconductivedrum with a toner which has been subjected to frictionalelectrification. The reference numeral 23 denotes an intermediatetransfer belt for conveying the toner image on the photoconductive drumto a transfer paper. The reference numeral 24 denotes a paper feedcassette which stores paper for forming the toner image. The referencenumeral 25 denotes a fixing machine which makes the toner imagetransferred onto the paper adhere to the paper with heat. The referencenumeral 26 is a paper discharge tray on which the fixed transfer paperis placed. The reference numeral 27 denotes a cleaner which cleans atoner remaining on the photoconductive drum. The reference numeral 28denotes a dustproof glass which is disposed at the laser light emittingaperture to the photoconductive drum in such a manner that the toner ordust does not adhere to optical members, such as a mirror or a lens,which are constituent components of the optical apparatus.

In image formation, an image is formed on the photoconductive drumelectrified by an electrifier by irradiating the photoconductive drumwith laser emission light by the optical apparatus 21 based on imageinformation. Thereafter, by attaching the toner to the image in thedevelopment machine 22, a toner image is formed on the photoconductivedrum. The toner image is transferred onto the intermediate transfer belt23 from the photoconductive drum. Then, by transferring the toner imageagain onto paper conveyed from the paper feed cassette 24, an image isformed on the paper. To the image transferred onto the paper, a toner isfixed by a fixation machine 25, and then placed on the paper dischargetray 26. The optical apparatus 21 has, in housing, a light source whichemits laser light based on image information, a rotary polygon mirrorfor deflecting and scanning the laser light emitted from the lightsource, and optical members, such as an fθ lens by which the laser lightdeflected and scanned by the rotary polygon mirror is imaged on aphotoreceptor and a reflecting mirror. In order to prevent the adhesionof dirt, such as dust and a toner, to the optical members, such as amirror or a lens, constituting the optical apparatus, a dustproof glass28 is provided at the laser light emitting aperture to thephotoconductive drum of the housing. When the toner scattering from thedevelopment machine or the like is accumulated on the dustproof glass,poor images are formed in which the dropping of the quantity of laserlight occurs or white spots are formed. Then, the porous body describedin the first embodiment is used for at least one portion of thedustproof glass disposed on the image forming apparatus. The porous bodymay be integrally formed as a film on the base material. For the basematerial, base materials having heat resistance, such as quartz glass,7059 glass of Corning, Inc., Neoceram N-0 of Nippon Electric Glass Co.,Ltd., sapphire, crystal, and the like.

In order to suitably use the same for the image forming apparatus, it isdesirable that the average skeleton diameter of the porous body surfaceis 5 nm or more and 80 nm or lower and more suitably the skeletondiameter is 5 nm or more and 50 nm or lower for the same reasons asthose of the first embodiment. It is also desirable that the averagepore diameter of the porous body surface is 5 nm or more and 500 nm orlower, particularly 10 nm or more and 100 nm or lower, and further 15 nmor more and 80 nm or lower. It is desirable that the porosity of theporous body is usually 10% or more and 80% or lower and particularly 20%or more and 75% or lower.

When an antireflection function is required, the reflection on theinterface with the air is reduced when the porosity is increased. Inthis case, the porosity is suitably 30% or more and more suitably 50% ormore.

Although the porous body has an excellent feature that dust, dirt, andthe like are hard to adhere thereto, an aspect may be used in which, byattaching a shutter or the like, the dustproof glass is protected fromdirt, such as a toner, and dust when the photoconductive drum is notrequired to be irradiated. A cleaning mechanism for wiping off dirt mayalso be attached. Since the porous body has high strength, the porousbody may bear the shock to the porous body by the shutter, the cleaningmechanism, and the like. The image forming apparatus of this embodimentmay further have the foreign substance removal apparatus describedabove.

Manufacturing Method

Hereinafter, a method for manufacturing the porous body is described.First, a method for manufacturing a member containing only the porousbody is described. The porous body is obtained by, for example, removingat least one phase of a phase separated glass which is phase separatedinto at least two phases.

Mentioned as the materials of a phase separable base glass are, forexample, a silicon oxide-boron oxide-alkali metal oxide, a siliconoxide-phosphate-alkali metal oxide, and the like as a silicon oxide baseglass. Among the above, it is suitable to use a borosilicate glass ofthe silicon oxide-boron oxide-alkali metal oxide for the phase separablebase glass.

The phase separable base glass may be manufactured by preparing rawmaterials in such a manner as to have the above-described composition,heating and melting the raw materials containing the supply source ofeach component, and molding the resultant substance into a desired shapeas required. The temperature for heating and melting may be determinedas appropriate in accordance with the raw material composition and thelike and is usually in the range of 1350° C. to 1450° C. andparticularly suitably in the range of 1380° C. to 1430° C. In thisdescription, the heating for melting the raw materials is referred to asheating and melting.

For example, sodium carbonate, boric acid, and silica dioxide may beuniformly mixed as the raw materials, and then the mixture is heated to1350° C. to 1450° C. for melting. In this case, any raw material may beused as the raw materials insofar as the raw materials contain alkalimetal oxide, boron oxide, and silicon oxide components as describedabove.

When the porous glass is formed into a predetermined shape, a phaseseparable base glass may be synthesized, and thereafter molded intovarious shapes, such as a tubular shape, a plate shape, a sphericalshape, and the like at a temperature of about 1000° C. to about 1200° C.For example, a method may be suitably employed which includes meltingthe raw materials mentioned above to synthesize a base glass, loweringthe temperature from the melting temperature, and then molding theresultant substance in a state where the temperature is maintained at1000° C. to 1200° C.

In general, the phase separation of the base glass is carried out byheat-treating the phase separable base glass. The “phase separation”means causing phase separation on the nm of scale of a silicon oxiderich phase and an alkali metal oxide-boron oxide rich phase in the glasswhen a borosilicate glass of a silicon oxide-boron oxide-alkali metaloxide is used for the base glass, for example. The heating temperaturefor phase separation for causing the phase separation is 400° C. to 800°C., and the heating time for phase separation may be usually determinedin the range of several hours to 100 hours in accordance with the porediameter or the like of the porous glass to be obtained. In thisdescription, the heating for causing the phase separation of the baseglass is referred to as heating for phase separation.

Thus, acid soluble components are eluted and removed by bringing thephase separable glass obtained by the process for heating for phaseseparation into contact with an acid solution. As the acid solution,inorganic acid, such as hydrochloric acid and nitric acid, may besuitably used, for example, and, in general, the acid solution may besuitably used in an aspect in which water is used as the solvent. Theconcentration of the acid solution may be determined as appropriate inthe range of 0.1 mol/L to 2 mol/L (0.1 to 2 normal). In the acidtreatment process for bringing the glass into contact with the acidsolution (etching treatment process), the temperature of the acidsolution may be set in the range of room temperature to 100° C. and thetreatment time may be set to about 1 hour to about 50 hours. Thereafter,the porous body having a skeleton of silicon oxide is obtained throughwater washing treatment. The temperature of the water for use in thewater washing treatment process may be generally set in the range ofroom temperature to 100° C. The time of the water washing treatmentprocess may be determined as appropriate in accordance with thecomposition, size, or the like of the target glass and may be generallyset to about 1 hour to about 50 hours.

In the heating for phase separation process, a layer of a silicon oxiderich phase which may not be removed by the acid treatment may be formedon the base glass surface. In this case, it is suitable that the layerof a silicon oxide rich phase is removed by polishing or the like, andthen the acid treatment is performed. As a polishing measure, mirrorfinish using CeO₂ powder is suitable.

The porous body may be manufactured without passing through thetreatment for heating for phase separation or the acid treatment. Themethod has a process for mixing 4% by weight or more and 20% by weightor lower of sodium oxide, 10% by weight or more and 40% by weight orlower of boron oxide, and 50% by weight or more and 80% by weight orlower of silicon oxide. Next, the method has a process for heating themixed materials for melting, and then cooling the mixture to obtain aphase separable base glass and a process for bringing the base glassinto contact with water without heating the same again to thereby obtaina porous body.

The porous body may be obtained by performing the water washingtreatment for bringing the base glass into contact with water. Accordingto the method, the porous body containing a porous body may be obtainedonly by performing the water washing treatment of the base glass withoutpassing through the treatment for heating for phase separation or theacid treatment by specifying the composition of the base glass in theabove-described composition range. As suitable compositions of the mixedmaterials and the base glass to be used in the manufacturing method, thecontent of sodium oxide is usually 4% by weight or more and 20% byweight or lower and particularly suitably 4.5% by weight or more and 15%by weight or lower. The content of boron oxide is usually 10% by weightor more and 40% by weight or lower and particularly suitably 12% byweight or more and 35% by weight or lower. The content of silicon oxideis usually 50% by weight or more and 80% by weight or lower andparticularly suitably 58% by weight or more and 75% by weight or lower.

By adopting the specific composition, the porous body may be obtainedonly by the water washing treatment without requiring the treatment forheating for phase separation and the acid treatment. In general, a layerwhich is hard to etch is formed on the surface of the phase separatedglass. After the layer is removed by a mechanical measure, such aspolishing, or a chemical measure, such as etching with hydrofluoric acidor an aqueous alkaline solution, etching with an aqueous acid solutionis performed. Suitably, the water washing treatment is usually performedusing water in a neutral region and immersing in an aqueous solution ofa temperature of 50° C. or higher and 100° C. or lower. The waterwashing treatment may be set to about 1 hour to about 50 hours.

In the sodium oxide-boron oxide-silicon oxide base glass, the totalcontent of sodium oxide, boron oxide, and silicon oxide is 95% by weightor more and 100% by weight or lower based on the total amount of thephase separated glass. The base glass may contain three ormore-component oxides in addition to the three-component oxidesmentioned above. For example, mentioned as a silicon oxide base glassare silicon oxide-boron oxide-alkali metal oxide-(alkaline earth metaloxide, zinc oxide, aluminum oxide, or zirconium dioxide), a titaniumoxide base glass (silicon oxide-boron oxide-calcium oxide-magnesiumoxide-aluminum oxide-titanium oxide), a rare earth base glass (boronoxide-alkali metal oxide-(cerium oxide, thorium oxide, hafnium oxide, orlanthanum oxide)), and the like. As a fourth component in addition tothe three components or more, aluminum oxide, zirconium oxide, alkalineearth metal oxide, and the like are mentioned, for example, but thefourth component is not limited thereto. The content of the fourthcomponent is lower than 5% by weight.

Even when the sodium oxide-boron oxide-silicon oxide-based phaseseparated glass in the above-described composition range is subjected toonly the water washing treatment without subjected to the heat treatmentor the acid treatment, the same porous body as that produced with ageneral manufacturing method may be obtained.

Next, a method for forming the porous body (porous glass layer) on thebase material is described.

In order to form the porous body (porous glass layer) on the basematerial, the method has a process including forming, on the basematerial, a glass powder layer containing, as the main components, glasspowder containing a basic glass obtained by at least mixing and meltingporous glass generation raw materials. The method further has a processfor obtaining the phase separated glass layer which is phase separatedby heat-treating the glass powder layer at a temperature equal to orhigher than the glass transition point of the glass powder and a processfor obtaining the porous glass layer of the spinodal structure havingcontinuous pores by etching the phase separated glass layer.

Mentioned as an example of the manufacturing method are all themanufacturing methods which may achieve the formation of a glass layer,such as a printing method, a vacuum deposition method, a sputteringmethod, a spin coating method, and a dip coating method, and anymanufacturing method may be used insofar as the structure of theembodiments may be achieved.

It is preferable to form the spinodal structure in the porous body onthe base material. The formation of the spinodal structure requiresprecise composition control of glass. A film formation method whichincludes determining the glass composition once, forming glass powder,and then melting the same is excellent in that the composition controlmay be easily performed.

The phase separated glass layer may be obtained which is phase separatedby heating the glass powder layer at a temperature equal to or higherthan the glass transition point of the glass powder. At a temperaturelower than the glass transition point of the glass powder, the meltingof the glass powder does not proceed, so that the layer formation is notperformed. In contrast, only by simply heating the glass powder, thephase separation is not performed, so that the porous body (porous glasslayer) of the spinodal structure may not be formed in some cases.

The present inventors have conducted extensive research, and as aresult, have found that the phenomenon of hindering the formation of thespinodal structure is caused by the crystallization in the heattreatment of the glass powder, for example, and the object of theembodiment is achieved by precisely controlling the heat treatmentconditions. More specifically, it is considered that since the phaseseparation phenomenon of glass occurs in the amorphous state, it isrequired to select a heat treatment method for forming a layer whilemaintaining the amorphous state when melting glass powder to form aporous body (glass layer). As the heat treatment method for forming alayer while maintaining the amorphous state, any method may be usedinsofar as the amorphous state may be maintained. Mentioned as anexample is a method for suppressing the formation of the crystal nucleusby performing the heat treatment at a temperature equal to or lower thanthe crystallization temperature or a method for suppressing theformation of the crystal nucleus by rapidly cooling glass from themelting state at a high temperature (crystallization temperature orhigher).

Hereinafter, an embodiment of the process for forming a glass powderlayer containing glass powder containing, as the main components, abasic glass obtained mixing and melting raw materials for generating theporous body (porous glass) is described. Specifically, a glass pastecontaining glass powder containing, as the main components, a basicglass obtained by at least mixing and melting the porous glassgeneration raw materials and a solvent is applied onto a base material,and then the solvent is removed to thereby form a glass powder layer.Mentioned as an example of a method for forming the glass powder layerare a printing method, a spin coating method, a dip coating method, andthe like.

Hereinafter, a method employing a general screen printing method isdescribed as an example of the method for forming the glass powder layercontaining glass powder.

According to the screen printing method, glass powder is formed into apaste, and then is printed using a screen printer. Therefore, thepreparation of the paste is indispensable.

The porous body (porous glass layer) is formed by the phase separationof glass. Therefore, it is suitable to use a phase separable base glasswhich may be phase separated as the glass powder for use in the glasspaste.

The materials of the phase separable base glass base material whichforms the spinodal structure are not particularly limited. For example,mentioned are a silicon oxide glass I (Base glass composition: siliconoxide-boron oxide-alkali metal oxide), a silicon oxide glass II (Baseglass composition: silicon oxide-boron oxide-alkali metaloxide-(alkaline earth metal oxide, zinc oxide, aluminum oxide, orzirconium oxide)), a titanium oxide glass (Base glass composition:silicon oxide-boron oxide-calcium oxide-magnesium oxide-aluminumoxide-titanium oxide), and the like. Among the above, a borosilicateglass of silicon oxide-boron oxide-alkali metal oxide is suitable.

In the borosilicate glass, glass having a composition such that theproportion of silicon oxide is 50.0% by weight or more and 80.0% byweight or lower and particularly 55.0% by weight or more and 75.0% byweight or lower is suitable. When the proportion of silicon oxide is inthe above-described range, there is a tendency that a phase separatedglass with high skeleton strength may be easily obtained. Therefore, theproportion is particularly useful for the case where strength isrequired.

As the method for manufacturing the phase separable base glass, thephase separable base glass may be manufactured using known methods,besides preparing the raw materials in such a manner as to have theabove-described composition. For example, the phase separable base glassmay be manufactured by heating and melting the raw materials containingthe supply source of each component, and molding the resultant substanceinto a desired shape as required. The heating temperature for heatingand melting may be determined as appropriate in accordance with the rawmaterial composition and the like and is usually in the range of 1300°C. to 1450° C. and particularly suitably in the range of 1320° C. to1430° C.

For example, sodium oxide, boric acid, and silica dioxide may beuniformly mixed as the raw materials, and then the mixture is heated to1300° C. to 1450° C. for melting. In this case, any raw material may beused as the raw materials insofar as the raw materials contain alkalimetal oxide, boron oxide, and silicon oxide components mentioned above.

When the phase separable base glass is formed into a predeterminedshape, the phase separable base glass may be synthesized, and thereaftermolded into various shapes, such as a tubular shape, a plate shape, aspherical shape, and the like at a temperature of about 1000° C. toabout 1200° C. For example, a method may be suitably employed whichincludes melting the raw materials mentioned above to synthesize thephase separable base glass, lowering the temperature from the meltingtemperature, and then molding the glass in a state where the temperatureis maintained at 1000° C. to 1200° C.

In the phase separated glass which is likely to be crystallized, it issuitable to use a rapidly cooling measure when lowering the temperaturefrom the melting temperature. By rapidly cooling, the formation of thecrystal nucleus in the glass may be suppressed, an amorphous uniformglass layer may be easily formed, and the phase separation may be easilyachieved.

In order to use the same as a paste, glass is crushed to obtain glasspowder. A crushing method is not required to be particularly limited,and known crushing methods may be used. Mentioned as an example of thecrushing method is a crushing method in a liquid phase typified by abead mill or a crushing method in a vapor phase typified by a jet mill.

In order to form the glass powder layer containing glass powder, theglass powder layer is formed using a paste containing the glass powder.The paste contains a thermoplastic resin, a plasticizer, a solvent, andthe like with the above-described glass powder.

It is desirable that the proportion of the glass powder contained in thepaste is in the range of 30.0% by weight or more and 90.0% by weight orlower and suitably in the range of 35.0% by weight or more and 70.0% byweight or lower.

The thermoplastic resin contained in the paste is a component whichincreases the film strength after drying and imparts flexibility. Usableas the thermoplastic resin are polybutyl metacrylate, polyvinyl butyral,polymethyl metacrylate, polyethyl metcrylate, ethyl cellulose, and thelike. The thermoplastic resin may be used alone or as a mixture of twoor more kinds thereof.

The content of the above-described thermoplastic resin contained in thepaste is suitably 0.1% by weight or more and 30.0% by weight or lower.When the content is lower than 0.1% by weight, the film strength afterdrying tends to become weak. When the content is larger than 30.0% byweight, residual components of the resin are likely to remain in theglass when forming the glass layer. Therefore, the content is notsuitable.

Mentioned as the plasticizer contained in the paste are butyl benzylphthalate, dioctyl phthalate, diisooctyl phthalate, dicapryl phthalate,dibutyl phthalate, and the like. These plasticizers may be used alone oras a mixture of two or more kinds thereof.

The content of the plasticizer contained in the paste is suitably 10.0%by weight or lower. By adding the plasticizer, the drying rate may becontrolled and the flexibility may be imparted to a dry film.

Mentioned as the solvent contained in the paste are terpineol,diethylene glycol monobutyl ether acetate, 2,2,4-trimethyl-1,3-pentadiolmonoisobutyrate, and the like. The solvents may be used alone or as amixture of two or more kinds thereof.

The content of the solvent contained in the paste is suitably 10.0% byweight or more and 90.0% by weight or lower. When the content is lowerthan 10.0% by weight, there is a tendency that a uniform film isdifficult to obtain. When the content exceeds 90.0% by weight, there isa tendency that a uniform film is difficult to obtain.

The paste may be produced by kneading the above-described materials at agiven ratio.

By applying the paste onto the base material using a screen printingmethod, and then drying and removing the solvent component of the paste,the glass powder layer containing the glass powder may be formed. Inorder to achieve the target film thickness, the glass paste may belaminated by applying the same by an arbitrary number of times, and thendried.

The temperature and the time for drying and removing the solvent may bechanged as appropriate in accordance with the solvent to be used. It issuitable that a leveling process at a temperature lower than thedecomposition temperature of the thermoplastic resin is provided toflatten the surface.

Next, a process for decomposing the resin of the glass powder layer, andthen heat-treating the same at a temperature equal to or higher than theglass transition point of the glass powder to thereby obtain a phaseseparated glass layer which is phase separated.

During the process, the glass powder melt, and phase separation iscaused, so that the phase separated glass layer is formed.

In the phase separation, there are binodal type phase separation withdiscontinuous fine pores and spinodal type phase separation withcontinuous pores.

Among the above, pores of a porous glass obtained by the spinodal typephase separation structure are three-dimensional network penetrationcontinuous fine pores which are connected from the surface to theinside, and the porosity may be arbitrarily controlled by changing theheat treatment conditions. Since the pores are three-dimensional networkpenetration continuous pores, high surface strength is imparted.

The decomposition temperature of the thermoplastic resin may be measuredusing a differential type differential thermal balance (TG-DTA) or thelike.

When melting the glass powder, a binder removing process is provided asappropriate in such a manner that a carbon component of the resin doesnot remain. When melting the glass powder, the glass powder isheat-treated suitably at a temperature equal to or higher than the glasstransition point of the glass powder and more suitably in the glasssoftening temperature region. When the temperature is lower than theglass transition point, the melting of the glass powder does notproceed, and there is a tendency that the glass layer is not formed.

The heat treatment temperature for heat-treating the glass powder is setto 200° C. or higher and 1000° C. or lower, for example. The heattreatment time may be determined as appropriate in accordance with thepore diameter or the like of the porous glass to be obtained in therange of 1 hour to 100 hours. The process for heat-treating the glasspowder also includes the phase separation process.

The heat treatment temperature does not need to be a fixed temperatureand may be continuously changed or the glass powder may undergo aplurality of different temperature stages.

Next, a process for etching the phase separated glass layer to therebyobtain the porous body (porous glass layer) of the spinodal structurehaving continuous pores is performed.

The porous glass layer is obtained by removing non-skeleton portions ofthe phase separated glass layer obtained by the heat treatment process.

As a measure for removing the non-skeleton portions, it is common toelute a soluble phase by bringing the glass into contact with an aqueoussolution. As a measure for bringing the glass into contact with theaqueous solution, a measure for immersing the glass in the aqueoussolution is common. However, the measure is not limited insofar as theglass and the aqueous solution are brought into contact with each other,such as applying an aqueous solution to the glass.

As the aqueous solution, any existing aqueous solution, such as water,an aqueous acid solution, and an aqueous alkaline solution, may be usedinsofar as a soluble phase may be eluted.

A plurality of processes for bringing the glass into contact with theaqueous solutions may be selected in accordance with the intended use.

In common etching of the phase separated glass, acid treatment issuitably used from the viewpoint that the load to non-soluble phaseportions is low and the viewpoint of the degree of selective etching. Bybringing the glass into contact with the aqueous acid solution, analkali metal oxide-boron oxide rich phase which is an acid solublecomponent is eluted and removed and, in contrast, high selective etchingproperties are obtained without deteriorating the stability in thenon-soluble phase.

As the aqueous acid solution, inorganic acid, such as hydrochloric acidand nitric acid, is suitable, for example. As the aqueous acid solution,it is suitable to usually use an aqueous solution containing water asthe solvent. The concentration of the aqueous acid solution may beusually set as appropriate in the range of 0.1 mol/L to 2.0 mol/L.Depending on the case, only water may be used.

In the acid treatment process, the temperature of the aqueous acidsolution may be set in the range of room temperature to 100° C. and thetreatment time may be set to about 1 hour to 500 hours.

In general, it is suitable to perform treatment with the aqueous acidsolution, the aqueous alkaline solution, or the like (etching process1), and then perform water treatment (etching process 2). By performingthe water treatment, residual components in the porous glass skeletonmay be removed, so that a more stable porous body (porous glass) tendsto obtain.

The temperature in the water treatment process is generally suitably inthe range of room temperature to 100° C. The water treatment processtime may be suitably determined as appropriate in accordance with thecomposition, size, or the like of the target glass and may be usuallyset to 1 hour to 50 hours.

Moreover, a plurality of times of etching processes may be performed asrequired.

EXAMPLES

First, various evaluation methods in Example 1 to Example 3 aredescribed.

Measurement Method of Glass Transition Point (Tg) of Glass Powder

The glass transition point (Tg) of glass powder is measured from the DTAcurve measured by a differential type differential thermal balance(TG-DTA). As a measuring apparatus, Thermoplus TG8120 (RigakuCorporation) may be used, for example.

Specifically, the glass powder was heated at a temperature elevationrate of 10° C./minute from room temperature using a platinum pan tothereby measure the DTA curve. In the curve, the endothermic initiationtemperature at the endothermic peak was determined by extrapolation by atangent method to be used as the glass transition point (Tg).

Measurement Method of Crystallization Temperature

The crystallization temperature of glass powder is calculated asfollows.

The glass powder is heat-treated at 300° C. for 1 hour. The obtainedsample was evaluated by an X ray diffraction structure analysisapparatus (XRD). When the peak obtained from the crystal was notobserved, another glass powder was heat-treated at 350° C. which was 50°C. higher for 1 hour and evaluated by the XRD.

The operation was repeated until the crystal was confirmed, and thetemperature at which the peak obtained from the crystal was confirmedwas defined as the crystallization temperature. As a measuringapparatus, RINT2100 (Rigaku Corporation) may be used as the XRD, forexample.

Measurement Method of Porosity

Treatment for binarizing an electronograph at a skeleton portion and apore portion was performed. Specifically, the surface of the porousglass is observed at a magnification of 100,000 times (depending on thecase, 50,000 times) at which the contrast of the skeleton is easilyobserved at an accelerating voltage of 5.0 kV using a scanning electronmicroscope (FE-SEM S-4800, manufactured by Hitachi).

The observed image is saved as an image, and then the SEM image isgraphed at the frequency of each image density using an image analyzingsoftware. FIG. 12 is a view illustrating the frequency of each imagedensity of the porous body of the spinodal type phase separationstructure. The peak portion indicated by the downward arrow of the imagedensity of FIG. 12 represents the skeleton portion located at the front.

The bright portion (skeleton portion) and the dark portion (poreportion) are monochromatically binarized at the inflection point nearthe peak position as the threshold value. The average value of theentire image for the ratio of the black portion area to the entire area(total of the white portion area and the black portion area) wasdetermined to be used as the porosity.

Measurement Method of Pore Diameter and Skeleton Diameter

Images (electronographs) were taken at magnifications of 50,000 times,100,000 times, and 150,000 times at an accelerating voltage of 5.0 kVusing a scanning electron microscope (FE-SEMS-4800, manufactured byHitachi). 30 or more points of the width of the pore portions of theporous body were measured from the taken images, and the average valuewas defined as the pore diameter.

Similarly, 30 or more points of the width of skeleton portions of theporous body were measured from the taken images, and the average valuewas used as the skeleton diameter.

Measurement Method of Glass Layer Thickness

SEM images (electronographs) were taken at magnifications of 10,000times to 150,000 times at an accelerating voltage of 5.0 kV using ascanning electron microscope (FE-SEMS-4800, manufactured by Hitachi). 30or more points of the thickness of the glass layer portion on the basematerial were measured from the taken images, and the average value wasused as the glass layer thickness.

Measurement Method of Main Elements

The measurement of the main element constituting the base material andthe main elements constituting the porous glass layer may be measured byperforming a quantitative analysis of the constituent elements using anX ray photoelectron spectrum apparatus (XPS), for example. As ameasuring apparatus, ESCALAB 220 i-XL (manufactured by ThermoScientific) is used.

A specific measurement method is described. First, the main elementsconstituting the porous glass layer are analyzed by analyzying theelements of the top surface of the structure by XPS.

Subsequently, the glass layer on the top surface is removed by anarbitrary method, such as polishing, and the removal of the glass layeris confirmed by SEM or the like. Thereafter, the XPS measurement isperformed again to analyze the main elements of the base material. Or,the main elements of the base material may be analyzed by performing theXPS measurement of the base material portion of the cross section of thestructure.

Measurement Method of Surface Reflectance

The surface reflectance at a wavelength of 550 nm was measured using alens reflectance meter (manufactured by USPM-RUIII, Olympus, Inc.)

Hereinafter, the embodiment is described with reference to Examples butis not limited to Examples.

Example 1

Sodium carbonate, boric acid, and silica dioxide were used as glass rawmaterials, and were uniformly mixed at a composition ratio ofNa₂O:B₂O₃:SiO₂:Al₂O₃=7.3:27.2:62.5:3.0 (% by weight). Then, the mixturewas heated and melted at 1350° C. to 1450° C., and thereafter naturallycooled in a state where the mixture was molded into a plate shape,thereby obtaining an about 1 mm thick plate glass.

A base glass of a composition of 7.3Na₂O.27.2B₂O₃.62.5SiO₂.3.0Al₂O₃ (%by weight) obtained by cutting the plate glass into about 1 cm squarepieces was heated at 540° C. for 50 hours. In order to remove a surfacelayer, the glass was subjected to surface polishing. The glass wasimmersed in 1 N nitric acid warmed at 80° C. for 30 hours, and thenrinsed with ion exchange water, thereby obtaining a porous glass. Theresults of observing the glass surface of the obtained porous glassunder an electron microscope are shown in FIG. 6. It was found that thespinodal structure was formed. The skeleton diameter was 40 nm, the porediameter was 30 nm, and the porosity was 35%.

The obtained porous body was allowed to absorb water, and then crackscaused by the water absorption was confirmed but cracks were notobserved.

The obtained porous glass and a silica glass which is not a porous bodywere exposed to the atmosphere for 2 hours, and then a photograph ofdust in a 2 cm×2 cm region was taken. Then, when the number of the dustwas counted, the number of the dust adhering to the silica glass whichis not a porous body was 666 but the number of the dust adhering to theobtained porous glass was 43.

The surface reflectance of the obtained porous glass was 0.6%.

Example 2

Sodium carbonate, boric acid, and silica dioxide were used as glass rawmaterials, and were uniformly mixed at a composition ratio ofNa₂O:B₂O₃:SiO₂:Al₂O₃=9:30.5:59:1.5 (% by weight). Then, the mixture washeated and melted at 1350° C. to 1450° C., and then naturally cooled ina state where the mixture was molded into a plate shape, therebyobtaining an about 1 mm thick plate glass.

A base glass of a composition of 9Na₂O.30.5B₂O₃.59SiO₂.1.5Al₂O₃ (% byweight) obtained by cutting the plate glass into about 1 cm squarepieces was phase separated at 560° C. for 25 hours. In order to remove asurface layer, the glass was subjected to surface polishing. The glasswas immersed in 1 N nitric acid warmed at 80° C. for 50 hours, and thenrinsed with ion exchange water, thereby obtaining a porous glass. Whenobserving the glass surface of the obtained porous glass under anelectron microscope, it was found that the spinodal structure was formedsimilarly as in Example 1. The skeleton diameter was 35 nm, the porediameter was 50 nm, and the porosity was 55%.

The obtained porous glass and a silica glass which is not a porous bodywere exposed to the atmosphere for 2 hours, and then a photograph ofdust in a 2 cm×2 cm region was taken. Then, when the number of the dustwas counted, the number of the dust adhering to the silica glass whichis not a porous body was 754 but the number of the dust adhering to theobtained porous glass was 55.

The surface reflectance of the obtained porous glass was 0.5%.

Example 3

Sodium carbonate, boric acid, and silica dioxide were used as glass rawmaterials, and were uniformly mixed at a composition ratio ofNa₂O:B₂O₃:SiO₂=9.3:28.8:62.9 (% by weight). Then, the mixture was heatedand melted at 1350° C. to 1450° C., and then naturally cooled in a statewhere the mixture was molded into a plate shape, thereby obtaining anabout 1 mm thick plate glass.

A base glass of a composition of 9.3Na₂O.28.8B₂O₃.62.9SiO₂ (% by weight)obtained by cutting the plate glass into about 1 cm square pieces wasphase separated at 580° C. for 40 hours for phase separation. In orderto remove a surface layer, the glass was subjected to surface polishing.The glass was immersed in 1 N nitric acid warmed at 80° C. for 50 hours,and then rinsed with ion exchange water, thereby obtaining a porousglass. When observing the glass surface of the obtained porous glassunder an electron microscope, it was found that the spinodal structurewas formed similarly as in Example 1. The skeleton diameter was 45 nm,the pore diameter was 50 nm, and the porosity was 50%.

The obtained porous glass and a silica glass which is not a porous bodywere exposed to the atmosphere for 2 hours, and then a photograph ofdust in a 2 cm×2 cm region was taken. Then, when the number of the dustwas counted, the number of the dust adhering to the silica glass whichis not a porous body was 350 but the number of the dust adhering to theobtained porous glass was 36.

The surface reflectance of the obtained porous glass was 0.6%.

Next, enforcement methods and evaluation methods in Example 4 to Example9 are described.

Production Example of Glass Powder 1

A mixed powder containing quartz powder, boron oxide, sodium oxide, andalumina was melted at 1500° C. for 24 hours using a platinum crucible insuch a manner as to have a charge composition of 64% by weight SiO₂, 27%by weight B₂O₃, 6% by weight Na₂O, and 3% by weight Al₂O₃. Thereafter,the temperature of the glass was lowered to 1300° C., and then pouredinto a graphite mold. The mold was allowed to cool in the air for about20 minutes, held in a 500° C. slow cooling furnace for 5 hours, and thenallowed to cool over 24 hours. A block the obtained borosilicate glasswas crushed using a jet mill until the average particle diameter was 4.5μm, thereby obtaining a glass powder 1.

The crystallization temperature of the glass powder 1 was 800° C.

Production Example of Glass Powder 2

A glass powder 2 was obtained in the same manner as in the glass powder1, except using a mixed powder containing quartz powder, boron oxide,and sodium oxide in such a manner as to have a charge composition of63.0% by weight SiO₂, 28.0% by weight B₂O₃, and 9.0% by weight Na₂O.

The crystallization temperature of the glass powder 2 was 750° C.

Production Example of Glass Paste 1

Glass powder 1 60.0 parts by mass α-terpineol 44.0 parts by mass Ethylcellulose  2.0 parts by mass (Registered trade mark: ETHOCEL Std 200(manufactured by Dow Chemical Co.))

The raw materials were stirred and mixed, thereby obtaining a glasspaste 1. The viscosity of the glass paste 1 was 31300 mPa·s.

Production Example of Glass Paste 2

A glass paste 2 was obtained in the same method as in the glass paste 1,except using the glass powder 2 in place of the glass powder 1. Theviscosity of the glass paste 2 was 38000 mPa·s.

Examples of Base Materials 1 to 4

A quartz substrate (manufactured by IIYAMA PRECISION GLASS Co., Ltd.,Softening point: 1700° C.) was used as a base material 1.

A sapphire substrate (manufactured by Techno Chemics, Melting point:2030° C.) was used as a base material 2.

A glass substrate (Registered trade mark 7059, manufactured by Corning,Inc., Softening point: 844° C.) was used as a base material 3.

A glass substrate (Registered trade mark S-TIM 1, manufactured by OharaInc., Softening point: 699° C.) was used as a base material 4.

Three pieces of each substrate having a thickness of 1.1 mm which wascut into a size of 50 mm×50 mm, and then subjected to mirror finish wereused.

Production Example of Structure 1

The glass paste 1 was applied onto the base material 1 by screenprinting. As a printing machine, MT-320TV manufactured by MICRO-TEC Co.,Ltd. was used. As a plate, a solid image of 30 mm×30 mm of #500 wasused.

Subsequently, the resultant substance was allowed to stand still in a100° C. drying furnace for 10 minutes to dry the solvent. The filmthickness of the formed film was 10.00 μm as measured by SEM.

As a heat treatment process 1, the temperature was increased to 700° C.at a temperature elevation rate of 20° C./min, and then the film washeat-treated for 1 hour. Thereafter, as a heat treatment process 2, thetemperature was lowered to 600° C. at a temperature lowering rate of 10°C./min, and then the film was heat-treated at 600° C. for 50 hours.Then, the top surface of the film was polished, thereby obtaining aphase separable glass layer 1.

The phase separable glass layer 1 was immersed in a an aqueous 1.0 mol/Lnitric acid solution heated to 80° C., and then allowed to stand stillat 80° C. for 24 hours. Subsequently, the glass layer was immersed indistilled water heated to 80° C., and then allowed to stand still for 24hours. Then, a glass body was taken out from the aqueous solution, driedat room temperature for 12 hours, thereby obtaining a structure 1 inwhich a porous glass film was formed on a base material.

When the film thickness was observed by SEM, the formation of a uniformfilm having a film thickness of 7.00 μm was confirmed. The manufacturingconditions of the structure 1 are shown in Table 1. The measurementresults of each evaluation of the obtained structure 1 are shown inTable 2.

Production Example of Structure 2

A structure 2 in which a porous glass film was formed on a base materialwas obtained in the same manner as in the structure 1, except extendingthe polishing time of the top surface of the film when producing thephase separable glass layer 1. The film thickness was 0.09 μm asobserved by SEM. The measurement results of each evaluation of theobtained structure 2 are shown in Table 2.

Production Example of Structures 3 to 5

Structures 3 to 5 in which a porous glass film was formed on a basematerial were obtained in the same manner as in the structure 1, exceptchanging the production conditions as shown in Table 1. The measurementresults of each evaluation of the obtained structures are shown in Table2.

Production Example of Structure 6

A structure 6 in which a porous glass film was formed on a base materialwas obtained in the same manner as in the structure 1, except changingthe base material to be used from the base material 1 to the basematerial 2. The measurement results of each evaluation of the obtainedstructure 6 are shown in Table 2.

TABLE 1 Structure 1 Structure 2 Structure 3 Structure 4 Structure 5Structure 6 Substrate Type Base Base Base Base Base Base material 1material 1 material 1 material 1 material 1 material 2 Softening 17001700 1700 1700 1700 2030 point (Melting point) Paste Type Paste 1 Paste1 Paste 1 Paste 2 Paste 2 Paste 1 Softening 470 470 470 500 500 470temperature Crystallization 800 800 800 750 750 800 temperature HeatHeat Temperature 700 700 700 700 700 700 treatment treatment (° C.)conditions process 1 Time (hr) 1 1 1 1 1 1 Heat Temperature 600 600 575600 620 600 treatment (° C.) process 2 Time (hr) 50 50 25 50 50 50 Phaseseparation 700 700 700 700 700 700 temperature (° C.)

TABLE 2 Structure 1 Structure 2 Structure 3 Structure 4 Structure 5Structure 6 Substrate Type Base Base Base Base Base Base material 1material 1 material 1 material 1 material 1 material 2 Main element SiSi Si Si Si Al Softening 1700 1700 1700 1700 1700 2030 point (Meltingpoint) Young's 72 72 72 72 72 470 modulus (GPa) Glass film Main elementSi Si Si Si Si Si Porosity (%) 52 52 34 66 72 53 Pore 45 45 15 90 120 42diameter (nm) Skeleton 30 30 30 60 80 32 diameter (nm) Film 7.00 0.096.90 6.60 6.60 7.00 thickness (μm)

Example 4

The obtained structure 1 was evaluated by the following evaluationmeasures.

Evaluation of Fine Pore Structure

SEM images (electronographs) were taken at magnifications of 10,000 to150,000 times at an accelerating voltage of 5.0 kV using a scanningelectron microscope (FE-SEMS-4800, manufactured by Hitachi). From thetaken images, a continuous fine pore structure by spinodal type phaseseparation was judged.

Rank A: A continuous fine pore structure by spinodal type phaseseparation is confirmed.

Rank B: A continuous fine pore structure by spinodal type phaseseparation is not confirmed.

Evaluation of Structure Distortion

The structure distortion was evaluated according to the followingjudgment criterion. The structure was placed on a flat stand, and thedistortion was judged by whether or not the structure curves.

Rank A: Curvature of structure is not confirmed.

Rank B: Curvature of structure is confirmed.

Evaluation of Strength

The strength of the structure was evaluated by whether or not thestructure was destroyed when 10 mm portions of the sides facing eachother of the obtained structure were fixed, and a 100 g weight of anarea of 10 mm×10 mm was placed at the center of the structure.

Rank A: The structure is not destroyed.

Rank B: The structure is destroyed.

Evaluation of Film Adhesion

The interface of the porous glass layer portion and the base material ofthe obtained structure was observed using SEM to thereby evaluate thefilm adhesion. The evaluation criteria are as follows.

As an apparatus, a field emission scanning electron microscope S-4800(trade name) manufactured by Hitachi High-Technologies Corporation wasused, the observation was performed at a magnification of 150000 timesat an accelerating voltage of 5.0 kV. Specifically, the film adhesionwas judged by whether or not the interface of the skeleton portion ofthe porous glass layer and the base material is observed.

Rank A: The interface of the porous glass skeleton portion and the basematerial is not observed.

Rank B: The interface of the porous glass skeleton portion and the basematerial is clearly observed.

Dustproof Evaluation

One sheet of the structure 4 and a 5 cm×5 cm silica glass which is not aporous body were exposed to the atmosphere for 4 hours, and thereafter,a 20 mm×20 mm region was photographed, and the number of dust in theregion was counted.

Rank A: The number of the dust is 1/10 or lower relative to the numberof the dust on the silica glass.

Rank B: The number of the dust is larger than 1/10 and smaller than ⅕relative to the number of the dust on the silica glass.

Rank C: The number of the dust is ⅕ or more relative to the number ofthe dust on the silica glass.

Examples 5 to 9

The structures 2 to 6 were evaluated by the same evaluation measure asthat of Example 4. The evaluation results are shown in Table 3.

TABLE 3 Example 4 Example 5 Example 6 Example 7 Example 8 Example 9Silica Structure 1 Structure 2 Structure 3 Structure 4 Structure 5Structure 6 Glass Pore structure A A A A A A Structure A A A A A Adistortion Strength A A A A A A Film adhesion A A A A A B Dustproof A AA B B A C properties

Example 10

A porous glass was obtained by the same process as in Example 1, exceptheating a base glass at 520° C. for 80 hours for phase separation. Whenthe glass surface of the obtained porous glass was observed under anelectron microscope, it was found that the spinodal structure was formedsimilarly as in Example 1. The skeleton diameter was 10 nm, the porediameter was 20 nm, and the porosity was 35%.

The obtained porous glass and the silica glass which is not a porousbody were exposed to the atmosphere for 2 hours, and then dust in a 2cm×2 cm region was photographed. When the number of the dust wascounted, the number of the dust adhering to the silica glass which isnot a porous body was 620 and, in contrast, the number of the dustadhering to the obtained porous glass was 20.

The surface reflectance of the obtained porous glass was 0.8%.

Example 11

A porous glass was obtained by the same process as in Example 1, exceptheating a base glass at 600° C. for 30 hours for phase separation. Whenthe glass surface of the obtained porous glass was observed under anelectron microscope, it was found that the spinodal structure was formedsimilarly as in Example 1. The skeleton diameter was 70 nm, the porediameter was 60 nm, and the porosity was 60%.

The obtained porous glass and the silica glass which is not a porousbody were exposed to the atmosphere for 2 hours, and then dust in a 2cm×2 cm region was photographed. When the number of the dust wascounted, the number of the dust adhering to the silica glass which isnot a porous body was 620 and, in contrast, the number of the dustadhering to the obtained porous glass was 100.

The surface reflectance of the obtained porous glass was 0.5%.

Example 12

A porous glass was obtained by the same process as in Example 1, exceptheating a base glass at 470° C. for 25 hours for phase separation. Whenthe glass surface of the obtained porous glass was observed under anelectron microscope, it was found that the spinodal structure was formedsimilarly as in Example 1. The skeleton diameter was 2 nm and the porediameter was 6 nm. The porosity was unmeasurable.

The obtained porous glass and the silica glass which is not a porousbody were exposed to the atmosphere for 2 hours, and then dust in a 2cm×2 cm region was photographed. When the number of the dust wascounted, the number of the dust adhering to the silica glass which isnot a porous body was 623 and, in contrast, the number of the dustadhering to the obtained porous glass was 175. It is considered thatsince the skeleton diameter was small and dust was attached over two ormore skeletons, the number of the dust adhering thereto was larger thanthat of Examples 1 and 11.

The surface reflectance of the obtained porous glass was 1.2%.

Example 13

A porous glass was obtained by the same process as in Example 1, exceptheating a base glass at 610° C. for 50 hours for phase separation. Whenthe glass surface of the obtained porous glass was observed under anelectron microscope, it was found that the spinodal structure was formedsimilarly as in Example 1. The skeleton diameter was 100 nm, the porediameter was 100 nm, and the porosity was 70%.

The obtained porous glass and the silica glass which is not a porousbody were exposed to the atmosphere for 2 hours, and then dust in a 2cm×2 cm region was photographed. When the number of the dust wascounted, the number of the dust adhering to the silica glass which isnot a porous body was 600 and, in contrast, the number of the dustadhering to the obtained porous glass was 180.

The surface reflectance of the obtained porous glass was 0.6%.

The above results showed that the structures having the spinodal typestructure had high strength and a high dustproof effect. It was alsofound that the structures having a skeleton diameter of 5 nm or more and80 nm or lower had a high dustproof effect.

While the disclosure has been described with reference to exemplaryembodiments, it is to be understood that the disclosure is not limitedto the disclosed exemplary embodiments. The scope of the followingclaims is to be accorded the broadest interpretation so as to encompassall such modifications and equivalent structures and functions.

What is claimed is:
 1. An imaging apparatus comprising: an imagingelement; and a porous body having a three-dimensional skeleton, whereina plurality of continuous pores in three dimensions is in the porousbody.
 2. The imaging apparatus according to claim 1, wherein an averagediameter of the skeleton is 5 nm or more and 80 nm or lower.
 3. Theimaging apparatus according to claim 1, wherein an average diameter ofthe skeleton is 5 nm or more and 50 nm or lower.
 4. The imagingapparatus according to claim 1, wherein an average diameter of the poresis 5 nm or more and 500 nm or lower.
 5. The imaging apparatus accordingto claim 1, wherein a porosity of the porous body is 10% or more and 90%or lower.
 6. The imaging apparatus according to claim 1, wherein theskeleton contains silicon oxide.
 7. The imaging apparatus according toclaim 1, further comprising a base material on which the porous body isdisposed.
 8. The imaging apparatus according to claim 7, wherein thebase material contains crystal, sapphire or quartz glass.
 9. The imagingapparatus according to claim 1, further comprising an optical filter,wherein the optical filter is at least one of a low pass filter and aninfrared cut filter.
 10. The imaging apparatus according to claim 1,further comprising an optical filter, wherein the porous body, theoptical filter and the imaging element are arranged in this order. 11.The imaging apparatus according to claim 1, further comprising a devicefor removing a foreign substance.
 12. The imaging apparatus according toclaim 11, wherein the device is disposed between the imaging element andthe porous body.
 13. The imaging apparatus according to claim 11,wherein the device comprises a vibration member and is disposed in sucha manner that the vibration member contacts the porous body.
 14. Theimaging apparatus according to claim 11, further comprising an opticalfilter, wherein the porous body is arranged on an opposite side of theimaging element with respect to the optical filter, and wherein thedevice comprises a vibration member and is disposed in such a mannerthat the vibration member contacts the optical filter.
 15. An imageforming apparatus, comprising: an optical apparatus used for forming animage by emitting light; and a porous body provided in the opticalapparatus, wherein the porous body has a three-dimensional skeleton,wherein a plurality of continuous pores in three dimensions is in theporous body.
 16. The image forming apparatus according to claim 15,wherein an average diameter of the skeleton is 5 nm or more and 80 nm orlower.
 17. The imaging apparatus according to claim 15, wherein anaverage diameter of the pores is 5 nm or more and 500 nm or lower. 18.The image forming apparatus according to claim 15, further comprising abase material on which the porous body is disposed.
 19. The imageforming apparatus according to claim 18, wherein the base materialcontains crystal, sapphire or quartz glass.
 20. The imaging formingapparatus according to claim 15, further comprising a device forremoving a foreign substance.
 21. An imaging apparatus comprising: animaging element; a porous body having a three-dimensional skeleton; andan optical filter, wherein the optical filter is at least one of a lowpass filter and an infrared cut filter, and wherein a plurality ofcontinuous pores in three dimensions is in the porous body.
 22. An imageforming apparatus, comprising: an optical apparatus used for forming animage by emitting light; a porous body provided in the opticalapparatus; and a device for removing a foreign substance, wherein theporous body has a three-dimensional skeleton, wherein a plurality ofcontinuous pores in three dimensions is in the porous body.
 23. Theimaging apparatus according to claim 7, wherein the base material hascurvature.
 24. The imaging apparatus according to claim 18, wherein thebase material has curvature.
 25. The imaging apparatus according toclaim 21, wherein the base material has curvature.
 26. The imagingapparatus according to claim 22, wherein the base material hascurvature.